EP3798196A1 - Verres ayant des profils de contrainte non frangibles - Google Patents

Verres ayant des profils de contrainte non frangibles Download PDF

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Publication number
EP3798196A1
EP3798196A1 EP20205505.9A EP20205505A EP3798196A1 EP 3798196 A1 EP3798196 A1 EP 3798196A1 EP 20205505 A EP20205505 A EP 20205505A EP 3798196 A1 EP3798196 A1 EP 3798196A1
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EP
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Prior art keywords
glass
mol
mpa
dol
depth
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Granted
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German (de)
English (en)
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EP3798196B1 (fr
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Delena Lucinda Justice Duffy
Rostislav Vatchev Roussev
Vitor Marino Schneider
Kristy Lynn SMITH
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Corning Inc
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Corning Inc
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    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C21/00—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface
    • C03C21/001—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface in liquid phase, e.g. molten salts, solutions
    • C03C21/002—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface in liquid phase, e.g. molten salts, solutions to perform ion-exchange between alkali ions
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/083—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/083—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound
    • C03C3/085—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound containing an oxide of a divalent metal
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/083—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound
    • C03C3/085—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound containing an oxide of a divalent metal
    • C03C3/087—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound containing an oxide of a divalent metal containing calcium oxide, e.g. common sheet or container glass
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/089—Glass compositions containing silica with 40% to 90% silica, by weight containing boron
    • C03C3/091—Glass compositions containing silica with 40% to 90% silica, by weight containing boron containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/089—Glass compositions containing silica with 40% to 90% silica, by weight containing boron
    • C03C3/091—Glass compositions containing silica with 40% to 90% silica, by weight containing boron containing aluminium
    • C03C3/093—Glass compositions containing silica with 40% to 90% silica, by weight containing boron containing aluminium containing zinc or zirconium
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/095—Glass compositions containing silica with 40% to 90% silica, by weight containing rare earths
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/097—Glass compositions containing silica with 40% to 90% silica, by weight containing phosphorus, niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C4/00—Compositions for glass with special properties
    • C03C4/18—Compositions for glass with special properties for ion-sensitive glass
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C2204/00—Glasses, glazes or enamels with special properties

Definitions

  • the disclosure relates to strengthened glass. More particularly, the disclosure relates to strengthened glasses that do not exhibit frangible behavior.
  • Chemically strengthened glass is widely used as cover glass for mobile devices, touch-enabled displays, and the like.
  • non-frangible ion exchanged glass is preferred as a cover glass for touch-screen devices in order to reduce the risk of injury from small glass pieces due to self-accelerating highly fragmented fracture that is characteristic of highly-frangible stress conditions. Such conditions are often produced as a result of combinations of excessive compressive stress and center tension in the sample.
  • Recently disclosed criteria for non-frangibility based on a thickness-dependent maximum center tension (CT) are valid for relatively small thicknesses (i.e., ⁇ 0.8 mm) only in the regime when the depth of the compressive layer (DOL) achieved by chemical strengthening is substantially smaller than the sample thickness. For substantially larger depths of layer relative to the thickness.
  • CT thickness-dependent maximum center tension
  • a glass exhibiting non-frangible behavior in a region where substantially higher central tension is possible without reaching frangibility is provided. This region allows greater extension of the depth of compression in which fracture-causing flaws are arrested, without rendering the glass frangible despite the presence of high central tension region in the sample.
  • Strengthened glasses that have deep compressive layers and do not exhibit frangible behavior (i.e., the glasses are non- frangible) are provided.
  • the glasses have surface compressive layers extending from the surface to a depth of compression DOC that is at least about 0.08% of the total thickness of the glass, and a compressive stress CS and physical central tension CT, wherein CT-CS ⁇ 350 MPa.
  • one aspect of the disclosure is to provide a glass having a compressive layer extending from a surface of the glass to a depth of compression DOC and under a maximum compressive stress CS, a central region having a maximum physical central tension CT at a center of the glass, the central region extending outward from the center to the depth of compression, and a thickness t in a range from about 0.3 mm to about 1.0 mm, wherein DOC ⁇ 0.08 ⁇ t and CT-CS ⁇ 350 MPa.
  • a second aspect of the disclosure is to provide a glass having a compressive layer extending from a surface of the glass to a depth of compression DOC and under a maximum compressive stress CS, a central region having a maximum physical central tension CT at a center of the glass, the central region extending outward from the center to the depth of compression into the glass, and a thickness t in a range from about 0.3 mm to about 1.0 mm.
  • the depth of compression DOC is greater than or equal to 0.08 ⁇ t and the glass has an average elastic energy density of less than about 200 J/m 2 ⁇ mm.
  • a third aspect of the disclosure is to provide a glass comprising: a compressive layer extending from a surface of the glass to a depth of compression DOC, the compressive surface layer having a maximum compressive stress CS; a central region having a maximum physical central tension CT at a center of the glass. The central region extends outward from the center of the glass to the depth of compression.
  • the glass has a thickness t in a range from about 0.3 mm to about 1.0 mm, wherein DOC ⁇ 0.08 ⁇ t and CT-CS ⁇ 350 MPa.
  • the physical central tension CT is greater than 0.681 ⁇ (57 - 9.0 ⁇ ln( t ) + 49.3 ⁇ (ln( t )) 2 ) when 0.3 mm ⁇ t ⁇ 0.5 mm.
  • the physical central tension CT is greater than 0.728 ⁇ (57 - 9.0 ⁇ ln( t ) + 49.3 ⁇ (ln( t )) 2 ) when 0.5 mm ⁇ t ⁇ 0.7 mm.
  • the physical central tension CT is greater than 0.755 ⁇ ⁇ 38.7 MPa mm ⁇ ln t mm + 48.2 MPa when 0.7 mm ⁇ t ⁇ 1.0 mm.
  • a fourth aspect of the disclosure is to provide a glass comprising: a compressive layer extending from a surface of the glass to a depth of compression DOC, the compressive surface layer having a maximum compressive stress CS; a central region having a maximum physical central tension CT at a center of the glass, the central region extending outward from the center of the glass to the depth of compression, wherein the glass has an average elastic energy density of less than 200 J/m 2 ⁇ mm; and a thickness t in a range from about 0.3 mm to about 1.0 mm, wherein DOC ⁇ 0.08 ⁇ t.
  • the physical central tension CT is greater than 0.681 ⁇ (57 - 9.0 ⁇ ln( t ) + 49.3 ⁇ (ln( t )) 2 ).
  • the physical central tension CT is greater than 0.728 ⁇ (57 - 9.0 ⁇ ln( t ) + 49.3 ⁇ (ln( t )) 2 ), and when 7 mm ⁇ t ⁇ 1.0 mm, the physical central tension CT is greater than 0.755 ⁇ ⁇ 38.7 MPa mm ⁇ ln t mm + 48.2 MPa .
  • glass article and “glass articles” are used in their broadest sense to include any object made wholly or partly of glass. Unless otherwise specified, all compositions are expressed in terms of mole percent (mol%).
  • depth of layer and “DOL” refer to the depth of the compressive layer as determined by surface stress (FSM) measurements using commercially available instruments such as the FSM-6000.
  • depth of compression and "DOC” refer to the depth at which the stress within the glass changes compressive to tensile stress.
  • the stress crosses from a positive (compressive) stress to a negative (tensile) stress and thus has a value of zero.
  • Ion exchange is commonly used to chemically strengthen glasses.
  • alkali cations within a source of such cations e.g., a molten salt, or "ion exchange,” bath
  • CS compressive stress
  • potassium ions from the cation source are often exchanged with sodium ions within the glass.
  • the compressive layer extends from the surface to a depth within the glass and typically decrease from a maximum at the surface to 0 at the depth of compression DOC.
  • the strengthened glasses described herein has a maximum compressive stress of at least about 150 MPa and, in some embodiments, at least about 200 MPa. In certain embodiments, the compressive stress is less than about 250 MPa.
  • FIG. 1 A cross-sectional schematic view of a planar ion exchanged glass article is shown in FIG. 1 .
  • Glass article 100 has a thickness t, first surface 110, and second surface 112. While the embodiment shown in FIG. 1 depicts glass article 100 as a flat planar sheet or plate, glass article may have other configurations, such as three dimensional shapes or non-planar configurations.
  • Glass article 100 has a first compressive region 120 extending from first surface 110 to a depth of compression (DOC) d 1 into the bulk of the glass article 100.
  • DOC depth of compression
  • glass article 100 also has a second compressive region 122 extending from second surface 112 to a second depth of compression (DOC) d 2 .
  • DOC depth of compression
  • Glass article 100 also has a central region 130 that extends from d 1 to d 2 .
  • Central region 130 is under a tensile stress or physical central tension (CT), which balances or counteracts the compressive stresses of regions 120 and 122.
  • CT physical central tension
  • the depths di, d 2 of first and second compressive regions 120, 122 protect the glass article 100 from the propagation of flaws introduced by sharp impact to first and second surfaces 110, 112 of glass article 100, while the compressive stress minimizes the likelihood of a flaw penetrating through the depth di, d 2 of first and second compressive regions 120, 122.
  • the depth of compression DOC is at least about 8% of the total thickness t of the glass article - i.e., DOC ⁇ 0.8t - and, in certain embodiments, DOC ⁇ 0.8t when the thickness t is greater than 0.75 mm. In other embodiments, the depth of compression DOC is at least about 9% of the thickness t (DOC ⁇ 0.8t) and, in certain embodiments, DOC ⁇ 0.9t when the thickness t is greater than 0. 5 mm.
  • Compressive stress CS and depth of layer DOL are measured using those means known in the art.
  • Such means include, but are not limited to, measurement of surface stress (FSM) using commercially available instruments such as the FSM-6000, manufactured by Luceo Co., Ltd. (Tokyo, Japan), or the like, and methods of measuring compressive stress and depth of layer are described in ASTM 1422C-99, entitled “Standard Specification for Chemically Strengthened Flat Glass,” and ASTM 1279.19779 “Standard Test Method for Non-Destructive Photoelastic Measurement of Edge and Surface Stresses in Annealed, Heat-Strengthened, and Fully-Tempered Flat Glass ,” the contents of which are incorporated herein by reference in their entirety.
  • FSM surface stress
  • SOC stress optical coefficient
  • CT CS ⁇ DOL / t ⁇ 2 DOL
  • t is the thickness, expressed in microns ( ⁇ m), of the glass article.
  • central tensions CT and compressive stresses CS are expressed herein in megaPascals (MPa)
  • thickness t is expressed in either microns ( ⁇ m) or millimeters (mm)
  • depth of layer DOL is expressed in microns ( ⁇ m).
  • the FSM technique may suffer from contrast issues which affect the observed DOL value. At deeper DOL values, there may be inadequate contrast between the TE and TM spectra, thus making the calculation of the difference between TE and TM spectra - and determining the DOL - more difficult. Moreover, the FSM technique is incapable of determining the compressive stress profile (i.e., the variation of compressive stress as a function of depth within the glass). In addition, the FSM technique is incapable of determining the depth of layer resulting from the ion exchange of certain elements such as, for example, lithium.
  • the detailed index profiles are obtained from the mode spectra by using the inverse Wentzel-Kramers-Brillouin (IWKB) method.
  • IWKB inverse Wentzel-Kramers-Brillouin
  • the detailed index profiles are obtained by fitting the measured mode spectra to numerically calculated spectra of pre-defined functional forms that describe the shapes of the index profiles and obtaining the parameters of the functional forms from the best fit.
  • the birefringence n TM (z) - n TE (z) at any depth z is a small fraction (typically on the order of 1%) of either of the indices n TM (z) and n TE (z).
  • Obtaining stress profiles that are not significantly distorted due to noise in the measured mode spectra requires determination of the mode effective indices with precision on the order of 0.00001 RIU.
  • the methods disclosed in Roussev I further include techniques applied to the raw data to ensure such high precision for the measured mode indices, despite noise and/or poor contrast in the collected TE and TM mode spectra or images of the mode spectra. Such techniques include noise-averaging, filtering, and curve fitting to find the positions of the extremes corresponding to the modes with sub-pixel resolution.
  • Roussev II Unlike Roussev I, in which discrete spectra of modes are identified, the methods disclosed in Roussev II rely on careful analysis of the angular intensity distribution for TM and TE light reflected by a prism-sample interface in a prism-coupling configuration of measurements. The contents of the above applications are incorporated herein by reference in their entirety.
  • Roussev 1 and Roussev II comprise techniques for normalizing the intensity spectra, including normalizing to a reference image or signal, correction for nonlinearity of the detector, averaging multiple images to reduce image noise and speckle, and application of digital filtering to further smoothen the intensity angular spectra.
  • one method includes formation of a contrast signal, which is additionally normalized to correct for fundamental differences in shape between TM and TE signals.
  • the aforementioned method relies on achieving two signals that are nearly identical and determining their mutual displacement with sub-pixel resolution by comparing portions of the signals containing the steepest regions.
  • the birefringence is proportional to the mutual displacement, with a coefficient determined by the apparatus design, including prism geometry and index, focal length of the lens, and pixel spacing on the sensor.
  • the stress is determined by multiplying the measured birefringence by a known stress-optic coefficient.
  • derivatives of the TM and TE signals are determined after application of some combination of the aforementioned signal conditioning techniques.
  • the locations of the maximum derivatives of the TM and TE signals are obtained with sub-pixel resolution, and the birefringence is proportional to the spacing of the above two maxima, with a coefficient determined as before by the apparatus parameters.
  • the apparatus comprises several enhancements, such as using a light-scattering surface (static diffuser) in close proximity to or on the prism entrance surface to improve the angular uniformity of illumination, a moving diffuser for speckle reduction when the light source is coherent or partially coherent, and light-absorbing coatings on portions of the input and output facets of the prism and on the side facets of the prism, to reduce parasitic background which tends to distort the intensity signal.
  • the apparatus may include an infrared light source to enable measurement of opaque materials.
  • Roussev II discloses a range of wavelengths and attenuation coefficients of the studied sample, where measurements are enabled by the described methods and apparatus enhancements.
  • the range is defined by ⁇ s ⁇ ⁇ 250 ⁇ s , where ⁇ s is the optical attenuation coefficient at measurement wavelength ⁇ , and ⁇ s is the expected value of the stress to be measured with typically required precision for practical applications.
  • This wide range allows measurements of practical importance to be obtained at wavelengths where the large optical attenuation renders previously existing measurement methods inapplicable.
  • Roussev II discloses successful measurements of stress-induced birefringence of opaque white glass-ceramic at a wavelength of 1550 nm, where the attenuation is greater than about 30 dB/mm.
  • depth of layer and “DOL” as used herein refer to DOL values computed using the FSM technique
  • depth of compression and “DOC” refer to depths of the compressive layer determined by the methods described in Roussev I & II.
  • the glass articles may be chemically strengthened by ion exchange.
  • ions at or near the surface of the glass are replaced by - or exchanged with - larger ions having the same valence or oxidation state.
  • ions in the surface layer of the glass and the larger ions are monovalent alkali metal cations, such as Li + (when present in the glass), Na + , K + , Rb + , and Cs + .
  • monovalent cations in the surface layer may be replaced with monovalent cations other than alkali metal cations, such as Ag + or the like.
  • Ion exchange processes are typically carried out by immersing a glass article in a molten salt bath containing the larger ions to be exchanged with the smaller ions in the glass.
  • parameters for the ion exchange process including, but not limited to, bath composition and temperature, immersion time, the number of immersions of the glass in a salt bath (or baths), use of multiple salt baths, additional steps such as annealing, washing, and the like, are generally determined by the composition of the glass and the desired depth of layer and compressive stress of the glass that result from the strengthening operation.
  • ion exchange of alkali metal-containing glasses may be achieved by immersion in at least one molten bath containing a salt such as, but not limited to, nitrates, sulfates, and chlorides of the larger alkali metal ion.
  • a salt such as, but not limited to, nitrates, sulfates, and chlorides of the larger alkali metal ion.
  • the temperature of the molten salt bath typically is in a range from about 380°C up to about 450°C, while immersion times range from about 15 minutes up to about 40 hours. However, temperatures and immersion times different from those described above may also be used.
  • the compressive stress is created by chemically strengthening the glass article, for example, by the ion exchange processes previously described herein, in which a plurality of first metal ions in the outer region of the glass article is exchanged with a plurality of second metal ions so that the outer region comprises the plurality of the second metal ions.
  • Each of the first metal ions has a first ionic radius and each of the second alkali metal ions has a second ionic radius.
  • the second ionic radius is greater than the first ionic radius, and the presence of the larger second alkali metal ions in the outer region creates the compressive stress in the outer region.
  • At least one of the first metal ions and second metal ions are ions of an alkali metal.
  • the first ions may be ions of lithium, sodium, potassium, and rubidium.
  • the second metal ions may be ions of one of sodium, potassium, rubidium, and cesium, with the proviso that the second alkali metal ion has an ionic radius greater than the ionic radius than the first alkali metal ion.
  • Described herein are chemically strengthened glasses, such as Corning Gorilla® glass, that are used as a cover glass for mobile electronic devices and touch-enabled displays.
  • chemically strengthened glass is focusing on stress profiles with larger depth of the compression layer that help reduce the probability of explosive or frangible glass fracture when the device is dropped on a hard, rough surface.
  • Such fracture ejects glass pieces with substantial kinetic energy due to self-accelerating highly fragmented fracture that is characteristic of highly-frangible stress conditions produced as a result of combinations of excessive compressive stress and central tension in the glass.
  • Frangible behavior is characterized by at least one of: breaking of the strengthened glass article (e.g., a plate or sheet) into multiple small pieces (e.g., ⁇ 1 mm); the number of fragments formed per unit area of the glass article; multiple crack branching from an initial crack in the glass article; violent ejection of at least one fragment a specified distance (e.g., about 5 cm, or about 2 inches) from its original location; and combinations of any of the foregoing breaking (size and density), cracking, and ejecting behaviors.
  • the terms "frangible behavior” and "frangibility” refer to those modes of violent or energetic fragmentation of a strengthened glass article absent any external restraints, such as coatings, adhesive layers, or the like. While coatings, adhesive layers, and the like may be used in conjunction with the strengthened glass articles described herein, such external restraints are not used in determining the frangibility or frangible behavior of the glass articles.
  • FIGS. 10a and 10b Examples of frangible behavior and non-frangible behavior of strengthened glass articles upon point impact with a sharp indenter are shown in FIGS. 10a and 10b .
  • the point impact test that is used to determine frangible behavior includes an apparatus that is delivered to the surface of the glass article with a force that is just sufficient to release the internally stored energy present within the strengthened glass article. That is, the point impact force is sufficient to create at least one new crack at the surface of the strengthened glass sheet and extend the crack through the compressive stress CS region (i.e., depth of layer) into the region that is under central tension CT.
  • each ion exchanged glass plate shown in FIGS. 10a and 10b was subjected to a sharp dart indenter (e.g., a SiC indenter) contact sufficient to propagate a crack into the inner region of the plate, the inner region being under tensile stress.
  • a sharp dart indenter e.g., a SiC indenter
  • the force applied to the glass plate was just sufficient to reach the beginning of the inner region, thus allowing the energy that drives the crack to come from the tensile stresses in the inner region rather than from the force of the dart impact on the outer surface.
  • the degree of ejection may be determined, for example, by centering the glass sample on a grid, impacting the sample and measuring the ejection distance of individual pieces using the grid.
  • glass plate a can be classified as being frangible.
  • glass plate a fragmented into multiple small pieces that were ejected, and exhibited a large degree of crack branching from the initial crack to produce the small pieces. Approximately 50% of the fragments are less than 1mm in size, and it is estimated that about 8 to 10 cracks branched from the initial crack. Glass pieces were also ejected about 5 cm from original glass plate a, as seen in FIG. 10a .
  • a glass article that exhibits any of the three criteria (i.e., multiple crack branching, ejection, and extreme fragmentation) described hereinabove is classified as being frangible. For example, if a glass exhibits excessive branching alone but does not exhibit ejection or extreme fragmentation as described above, the glass is still characterized as frangible.
  • Glass plates b, c, ( FIG. 10b ) and d ( FIG. 10a ) are classified as not frangible. In each of these samples, the glass sheet has broken into a small number of large pieces.
  • Glass plate b ( FIG. 10b ) for example, has broken into two large pieces with no crack branching; glass plate c ( FIG. 10b ) has broken into four pieces with two cracks branching from the initial crack; and glass plate d ( FIG. 10a ) has broken into four pieces with two cracks branching from the initial crack.
  • samples b, c, and d are classified as non-frangible or substantially non-frangible.
  • a frangibility index (Table 1) can be constructed to quantify the degree of frangible or non-frangible behavior of a glass, glass ceramic, and/or a ceramic article upon impact with another object. Index numbers, ranging from 1 for non-frangible behavior to 5 for highly frangible behavior, have been assigned to describe different levels of frangibility or non-frangibility.
  • frangibility can be characterized in terms of numerous parameters: 1) the percentage of the population of fragments having a diameter (i.e., maximum dimension) of less than 1 mm (“Fragment size” in Table 1); 2) the number of fragments formed per unit area (in this instance, cm 2 ) of the sample ("Fragment density” in Table 1); 3) the number of cracks branching from the initial crack formed upon impact ("Crack branching” in Table 1); and 4) the percentage of the population of fragments that is ejected upon impact more than about 5 cm (or about 2 inches) from their original position ("Ejection” in Table 1). Table 1. Criteria for determining the degree of frangibility and frangibility index.
  • a frangibility index is assigned to a glass article if the article meets at least one of the criteria associated with a particular index value.
  • the article may be assigned a frangibility index range (e.g., a frangibility index of 2-3).
  • the glass article may be assigned the highest value of frangibility index, as determined from the individual criteria listed in Table 1. In many instances, it is not possible to ascertain the values of each of the criteria, such as the fragmentation density or percentage of fragments ejected more than 5 cm from their original position, listed in Table 1.
  • the different criteria are thus considered individual, alternative measures of frangible behavior and the frangibility index such that a glass article falling within one criteria level will be assigned the corresponding degree of frangibility and frangibility index. If the frangibility index based on any of the four criteria listed in Table 1 is 3 or greater, the glass article is classified as frangible.
  • glass plate a fragmented into multiple ejected small pieces and exhibited a large degree of crack branching from the initial crack to produce the small pieces. Approximately 50% of the fragments are less than 1 mm in size and it is estimated that about 8 to 10 cracks branched from the initial crack. Based upon the criteria listed in Table 1, glass plate a has a frangibility index of between about 4-5, and is classified as having a medium-high degree of frangibility.
  • a glass article having a frangibility index of less than 3 may be considered to be non-frangible or substantially non-frangible.
  • Glass plates b, c, and d each lack fragments having a diameter of less than 1 mm, multiple branching from the initial crack formed upon impact and fragments ejected more than 5 cm from their original position.
  • Glass plates b, c, and d are non-frangible and thus have a frangibility index of 1 (not frangible).
  • the observed differences in behavior between glass plate a, which exhibited frangible behavior, and glass plates b, c, and d, which exhibited non-frangible behavior, in FIGS. 10a and 10b can be attributed to differences in central tension CT among the samples tested.
  • the possibility of such frangible behavior is one consideration in designing various glass products, such as cover plates or windows for portable or mobile electronic devices such as cellular phones, entertainment devices, and the like, as well as for displays for information terminal (IT) devices, such as laptop computers.
  • the depth of the compression layer DOL and the maximum value of compressive stress CSs that can be designed into or provided to a glass article are limited by such frangible behavior.
  • the strengthened glass articles described herein exhibit a frangibility index of less than 3 when subjected to a point impact sufficient to break the strengthened glass article.
  • non-frangible strengthened glass articles may achieve a frangibility index less than 2 or less than 1.
  • an upper limit of the sum of CS and CT which allows indefinite increase of DOL without ever reaching frangibility is disclosed, including cases where the central tension CT increases very substantially above the CT frangibility limit most recently known, disclosed in recent patent application U.S. Patent No. 8,415,013 , entitled “Strengthened Glass Articles and Methods of Making” by Kristen Barefoot et al. (referred to hereinafter as "Barefoot I”), issued on April 9, 2013.
  • this upper limit of the sum of CS and CT is associated with an upper limit of the maximum spatial variation in K + concentration in a sample.
  • This spatial variation that is obtained by a single-step ion exchange of K + for Na + in a glass substrate in which Na + or Na + and K + are the only alkali ions in the glass.
  • an additional criterion for frangibility based on total stored elastic energy is introduced, allowing prediction of frangibility stress conditions in cases where the DOL is a substantial fraction of the sample thickness t. in one embodiment, DOL > 0.1t and, in other embodiments DOL > 0.15t. Under these conditions, frangibility conditions to be controlled for stress profiles obtained by either single-step or two-step ion exchange.
  • the total stored elastic energy criterion allows correct control of frangibility for stress profiles obtained by simultaneous or multi-step ion exchange involving counter diffusion of more than two ions.
  • the total-elastic-energy criterion allows quick non-destructive quality control of frangibility based on stress measurements such as prism coupling for single- and double-ion exchange compressive stress profiles having large depths of layer.
  • Barefoot I describes the frangibility limit for glass thicknesses smaller than about 0.75 mm, where an extrapolation of an earlier-known linear dependence found for larger thicknesses was found to under-estimate the upper limit of the non-frangible design space.
  • “Nonlinear threshold central tension CT 1” is given by the empirical formula CT 1 MPa ⁇ ⁇ 38.7 MPa / mm ⁇ ln t mm + 48.2 MPa where t is the sample thickness.
  • the frangibility limit CT 1 ranges from 48.2 MPa for a substrate thickness of 1 mm to 94.8 MPa for a thicknesses of 0.3 mm.
  • the onset of frangibility is observed when the DOL ranges between about 0.085t and 0.126t during ion exchange in nominally pure KNO 3 .
  • the ratio of CT A to the physical CT ranges from about 1.373 to about 1.469 over that range of DOL/t, averaging about 1.421.
  • the ratio CT/CT A ranges from about 0.681 to about 0.728, with an average value of about 0.704.
  • CT 1 For samples having a thickness greater than 0.75 mm and not greater than 1.0 mm, the relevant CT limit is CT 1 , described in Barefoot I.
  • the ratio of DOL/ t at which frangibility occurs in the examples of Barefoot I is typically in the range 0.048 to 0.060, and the ratio CT A /CT phys ranges from about 1.302 to about 1.324, the inverse of which ranges from 0.755 to 0.768.
  • the onset of frangibility may occur at substantially different CT A value for the glass having the same overall composition and thickness.
  • a 0.4-mm-thick substrate of the glass becomes frangible when ion exchanged in a bath containing essentially pure KNO 3 at 390°C to a depth of layer of about 36 ⁇ m, as measured by a FSM-6000 surface stress meter.
  • the compressive stress produced by the same surface stress meter during the measurement is about 920 MPa, and the CT A is about 101 MPa.
  • a sample having a thickness of 0.50 mm exhibited non-frangible behavior following ion exchange for 15.3 hours at 440°C in the ion exchange bath containing 37% NaNO 3 and 63% KNO 3 by weight.
  • the ion exchanged sample had CS of 304 MPa, DOL of 120.8 ⁇ m, and CT A of 142 MPa, which is substantially higher than the Barefoot II CT 3 limit of 86.9 MPa for 0.5 mm thick glass (Table 2).
  • a 0.4 mm-thick sample acquired a CS of 213 MPa, DOL of at least 149.3 ⁇ m, and CT A of at least 314 MPa following ion exchange for 21 hours at 440°C.
  • a 0.5 mm-thick substrate acquired a CS of 221 MPa, DOL of at least 147 ⁇ m, and CT A of at least 172 MPa following ion exchange for 25.25 hours at 440°C.
  • a substrate having a thickness of 0.6 mm acquired a CS of 254 MPa, DOL of at least 148 MPa, and CT A of at least 124 MPa, which is substantially greater than CT 3 of 74.5 MPa observed for 0.6mm thick glass.
  • a substrate with thickness of 0.8 mm acquired a CS of 272 MPa, DOL of at least 144 ⁇ m, and CT A of at least 76 MPa following ion exchange under the same conditions. This is substantially greater than the CT 1 value of 56.8 MPa observed for the same thickness and the CT 3 . Value of 59.3 MPa observed for a thickness of 0.75 mm.
  • a 1.0 mm thick substrate had a CS of 278 MPa, which is substantially greater than the CT 1 value of 48.2 MPa obtained for the same thickness, a DOL of at least 142 ⁇ m, and a CT A of at least 55 MPa.
  • the FSM-6000 instrument was unable to estimate the depth of layer and CT A for the deepest profiles.
  • the FSM-6000 usually underestimates DOL when DOL is greater than about 100 ⁇ m - and especially when the DOL is greater than 130 ⁇ m - due to the limited ability of the instrument to resolve the dark lines of the mode spectrum ,which become very dense when the DOL is very large.
  • samples of the same glass with greater thicknesses of 0.5, 0.6, 0.8, and 1.0 mm were ion exchanged for totals of 26 hours and 43 hours at 440°C in a bath containing 50 wt% NaNO 3 and 50 wt% KNO 3 . All of the samples were non-frangible. Because the depths of layer of these samples exceeded 150 ⁇ m, the DOL and CT A could not be measured on the FSM-6000 instrument.
  • the DOL as measured by the FSM-6000 exceeded 0.1t, and the CT A value at which frangibility was first observed was significantly higher than the CT 1 frangibility values determined by the empirical equations of Barefoot I and Barefoot II.
  • the actual physical central tension inside the mid-plane of the sample usually differs from the approximate value CT A , which has been widely adopted due to its ease of calculation based on the known thickness and the CS and DOL that are usually reported by the FSM-6000.
  • CT A the approximate value
  • the FSM-6000 estimates DOL from the measured number of guided optical modes in the ion-exchanged layer,.
  • the index profile differs from a linear truncated profile, especially at the deeper end of the profile.
  • the profile may be closely approximated by a complementary error function (erfc).
  • erfc complementary error function
  • the central tension CT for an erfc-shaped distribution of the K + concentration can be calculated by taking into account that the local change in specific volume is proportional to the local K + concentration and by applying the requirement of force balance, which requires that the spatial integral of the stress in the compression regions of the substrate be equal and opposite in sign to the integral of the stress over the tension region.
  • the ratio of the approximate adopted CT A and the calculated true physical CT (CT(erfc)) for the erfc profile characteristic of linear diffusion is shown in FIG. 2 as a function of the ratio of the depth of layer DOL, where DOL is calculated by the FSM-6000 for the same erfc-shaped index profile, with the FSM-6000 considering it as a linear truncated profile to the thickness of the layer.
  • CT CS 2 DOL 1.3825 t ⁇ 1 ⁇ e ⁇ 1.3825 2 t 2 4 DOL 2 2 DOL 1.3825 t ⁇ 1 ⁇ e ⁇ 1.3825 2 t 2 4 DOL 2 + erfc 1.3825 t 2 DOL ⁇ 1
  • CT A CS ⁇ DOL t ⁇ 2 DOL
  • CT A CT 1 1 ⁇ 2 DOL t DOL 0.69 t ⁇ 1 ⁇ e ⁇ 0.478 t 2 DOL 2 + erfc 0.69 t DOL ⁇ 1 0.816 1 ⁇ e ⁇ 0.478 t 2 DOL 2
  • Frangibility limit CT 1 in terms of CT A and the corresponding physical CT limit are calculated from CT 1 assuming the DOL is 0.03, 0.04, and 0.05 mm as commonly measured by the surface stress meter FSM-6000.
  • the CS is between about 700 and 900 MPa, and the DOL is greater than about 0.03 mm at the onset of frangibility.
  • FIG. 3 includes the separating line defined in terms of CT A according to Barefoot II ((a) in FIG. 3 ) and three other lines expressed in terms of physical CT and calculated for erfc-shaped profiles having the same CT A as Barefoot I are shown. These lines were calculated for different DOLs as measured by FSM-6000 and represent the range of typical DOLs for which frangibility occurs in the glass disclosed by Barefoot II following ion exchange in nominally pure KNO 3 . Of these, the highest CT limit representing the CT A curve in terms of physical CT is the one corresponding to the smallest DOL (0.03 mm; line b in FIG. 3 ).
  • FIG. 4 includes the separating line defined in terms of CT A ((a) in FIG. 3 ) as well as three other erfc-shaped profiles expressed in terms of physical CT. These profiles have the same CT A as the line a, and were calculated for different DOLs as measured by FSM-6000. These profiles represent the range of typical DOLs for which frangibility occurs in the glass disclosed in Barefoot II. Of the lines shown in FIG. 4 , the highest physical CT limit representing the CT A curve in terms of physical CT is the one corresponding to the smallest DOL.
  • substantially nonlinear diffusion occurs during the ion exchange of K + for Na + , where the mutual diffusion coefficient is low in regions with low K + concentrations, and is substantially higher in those regions where the K + concentration is a large fraction (> 25%) of the total concentration of K + and Na + .
  • the shape of the erfc function does accurate represent the shape of the index and stress profiles, and a detailed nonlinear diffusion model is necessary to accurately describe the profiles and their relationship to ion-exchange conditions.
  • FIG. 5 is a plot of transverse magnetic (TM) and transverse electric (TE) index profiles extracted by the IWKB-based algorithm up to the turning point of the last captured optical mode via prism coupling measurements.
  • the glass substrate was a 0.4-mm-thick glass that was ion exchanged 17.7 hours at 440°C in a bath containing 50% NaNO 3 and 50% KNO 3 by weight.
  • the glass substrate composition is described in U.S. Patent Application No. 13/678,013 .
  • the shapes of the index profiles differ substantially different from the erfc-shape.
  • FIG. 6 is a plot of a stress profile for a 0.4 mm-thick glass that was exchanged 17.7 hours at 440°C in a bath containing 50% NaNO 3 and 50% KNO 3 by weight.
  • the composition of the glass sample is described in U.S. Patent Application No. 13/678,013 .
  • This physical CT is substantially higher than the physical CT limit of 62 MPa, as taught by Barefoot et al., for a glass having a thickness of 0.4 mm.
  • the elastic energy per unit area, integrated along the depth dimension, is estimated to be about 13.4 J/m 2 in the compression region, and about 15.7 J/m 2 in the tension region. Hence, the total elastic energy is approximately 29.1 J/m 2 . Considering the thickness of 0.4 mm, the total elastic energy per unit thickness is 72.8 J/(m 2 ⁇ mm).
  • This physical CT in the general case, should correspond to the erfc-based physical CT that can be calculated in the essentially linear-diffusion case previously mentioned.
  • the stress profile found by the IWKB method is usually limited to the depth of the smaller of the deepest turning points for the TM and TE optical modes of the waveguide region. When the DOL is very large, the stress profile at depths approaching these largest depths is sometimes subject to significant noise.
  • FIG. 7 An example of the stress profile extracted using the IWKB method is shown in FIG. 7 .
  • the solid line (line a) in FIG. 7 represents the quadratic approximation adopted to emulate the profile shape in the tension zone for accurate estimate of the stress integral in the tension zone.
  • the variable part of the stress profile in the tension zone is represented by a parabola (dashed line (b) in FIG. 7 ) extending between the depth of compression (DOC) and the depth equal to 1.15 ⁇ DOL.
  • the depth of profile flattening is approximately 1.15 ⁇ DOL, where DOL is determined by the FSM-6000 instrument for the same ion exchanged glass.
  • DOL is determined by the FSM-6000 instrument for the same ion exchanged glass.
  • the deepest portion of the stress profile has a stress that approaches the central tension found by the above method of force balance between tension and compression forces.
  • the force balance condition represents the fact that, in the absence of external forces, the sample shape remains unchanged in time.
  • the difference CT-CS is about 305 MPa where, by traditional physics convention, tensile stress is positive and compressive stress negative. Frangibility never occurred during the ion exchange of glass at having a thickness of 0.4 mm in a bath containing 50 wt% NaNO 3 and 50 wt% KNO 3 , even when ion exchange times exceeded 30 hours and the stress profiles (at a level where the signal of the stress measurement is approximately equal to the noise level) from the two sides of the substrate approached very close to the center.
  • the concentration difference CT-CS
  • This difference remains largely independent of ion exchange time, until eventually the profiles from the two ends of the substrate meet in the middle and a measurable increase of the diffusant (K + , or K 2 O) concentration occurs in the center. At that point the concentration difference between the maximum concentration and the minimum concentration is reduced, and the difference CT-CS thus starts to decrease beyond that point even in the absence of stress relaxation.
  • a regime where the onset of frangibility may be limited not by achieving a CT required to propagate a flaw quickly through the tensile central region of the glass can be obtained, but rather by the amount of stored elastic energy when the DOL is large, generally DOL > 0.1t.
  • the CT may exceed the previously disclosed frangibility CT limit when the DOL is greater than about 0.15t. If the amount of stored elastic energy in the compression and tension regions is not adequate for the formation of large, new, free surfaces during crack propagation and bifurcation, then frangibility is prevented.
  • v is the Poisson ratio (0.22 for the exemplary glass composition described hereinabove)
  • E is Young's modulus (about 68 GPa for our example glass 5318)
  • ⁇ is the stress.
  • the total elastic energy stored in the substrate is twice the sum of the elastic energy of a single compression and the tension region, multiplied by 2 to account for two compression regions region and one half of the central tension region occurring in a chemically strengthened substrate.
  • For elastic energy per unit substrate area: W el MPa ⁇ 1 ⁇ MPa ⁇ 10 6 N m 2 ⁇ 10 ⁇ 6 m ⁇ N ⁇ m m 2 ⁇ J m 2 ⁇ ⁇ J mm 2 and For elastic energy per unit substrate area per unit thickness: J/m 2 ⁇ mm.
  • results obtained for glasses having thicknesses ranging from 0.4 to 1.0 mm are summarized in Table 3.
  • the glasses were ion exchanged at 440°C for various times in a bath containing about 45 wt% NaNO 3 and about 55 wt% KNO 3 .
  • the DOL determined by the FSM-6000 ranges from about 0.14t to about 0.39t.
  • the CT-CS difference ranges from about 311 MPa to at least 324 MPa.
  • the CS ranges from about 222 MPa to about 270 MPa. All glass samples listed in Table 3 were found to be non-frangible.
  • the physical CT exceeded the physical CT frangibility limit corresponding to prior art limits, and CT A exceeded the prior-art CT A limit.
  • the sample having a thickness of 0.4 mm exhibited a depth of compression DOC of 81.6 ⁇ m, physical CT of at least 102.7 MPa, stored elastic energy in the compression region of 15.1 J/m 2 , and stored elastic energy in half of the tension region of at least 8.9 J/m 2 .
  • the total elastic energy is at least 48 J/m 2 which, when normalized to thickness is at least 120 J/m 2 ⁇ mm.
  • a new non-frangible region where the DOL is greater than about 0.1t has been found for the thickness of 0.4 mm.
  • the ion exchange time of 26.5 hours at 440°C in a bath composed of about 50 wt-% NaNO 3 and 50 wt-% KNO 3 resulted in non-frangible glass with CS of about 191 MPa, a CT of at least 94 MPa, and a DOC of about 85 microns
  • a 0.4 mm thick sample ion exchanged for 26.5 hours at 440°C in a bath composed of about 50 wt% NaNO 3 and 50 wt% KNO 3 was non-frangible and had a CS of about 191 MPa, a CT of at least 94 MPa, and a DOC of about 85 ⁇ m.
  • Non-frangible and frangible glass with DOL > 0.1t and various thicknesses, after ion exchange in a bath containing about 40 wt% NaNO 3 and 60 wt% KNO 3 at 440 C are summarized in Table 4.
  • the examples that were ion exchanged for 42.6 hours have FSM-style DOL substantially above 150 ⁇ m, and some of the high-order modes may not have been detected due to difficulty resolving these densely spaced modes.
  • the calculated values of DOL, physical CT, tension energy, and total elastic energy are lower-limit estimates.
  • Non-frangible examples exhibit CT-CS values of up to 334 MPa.
  • the physical CT substantially exceeds previously reported corresponding CT limits for the thicknesses of 0.6mm (CT ⁇ 52 MPa), 0.8 mm (CT ⁇ 44.3 MPa), and 1.0 mm (CT ⁇ 38 MPa). Respectively.
  • a 0.4 mm thick glass sample ion exchanged in a bath composed of 40 wt% NaNO 3 and 60 wt% KNO 3 for 21.5 hours was found to be frangible, having a total stored elastic energy of about 56.2 J/m 2 which, when normalized to thickness, equaled about 140.4 J/m 2 mm.
  • the newly discovered non-frangible region is characterized as having stored elastic energy of less than 56.2 46.6 J/mm 2 for a 0.4 mm glass sample thickness, and the elastic energy normalized to thickness is less than 140.4 J/m 2 mm for all thicknesses, particularly for thicknesses greater than or equal to 0.4mm.
  • the DOC of the sample was as high as 91.6 ⁇ m, the energy in the compression region was 18.7 J/m 2 , and the energy in the tension half-region was at least 8.7 J/m 2 .
  • the total stored elastic energy was at least 54.8 J/m 2 which, when normalized to the thickness, was at least 109.7 J/m 2 ⁇ mm.
  • the CT-CS difference was about 316 MPa.
  • the ion exchanged sample had a CS of about 248 MPa, a DOL of about 153 ⁇ m, a DOC of 98.6 ⁇ m, and a physical CT of at least 65.6 MPa, the latter being substantially above the limit of about 51 MPa reported by Barefoot et al. in terms of physical CT for DOL of about 40 ⁇ m.
  • the CT A was estimated to be 130 MPa, which is substantially greater than the previously reported CT 3 of 75.5 MPa.
  • the estimated elastic energy in the compression region was 21.5 J/m 2 , and in the tension region it was approximately 8.1 J/m 2 .
  • the total elastic energy was about 59.4 J/m 2 , and elastic energy per unit area and unit thickness was about 98.9 J/m 2 mm.
  • a 0.6 mm thick sample listed in Table 4 was ion exchanged at 440°C for 25.7 hours in a bath comprising about 40 wt% NaNO 3 and about 60 wt% KNO 3 was found to be non-frangible.
  • the ion exchanged sample had a CS of about 255 MPa, a DOL close to 150 ⁇ m, a DOC of 100 ⁇ m, and even higher physical CT of about 70.2 MPa, which was substantially higher than the previously reported value of about 56 MPa.
  • the elastic energy in the compression region was about 24.2 J/m 2 , and at least 39.4 J/m 2 in the tension half-region.
  • the total elastic energy was estimated to be at least 67.3 J/m 2 , and the elastic energy per unit area and unit thickness was at least 112 J/m 2 mm.
  • Another sample listed in Table 4 and having the same 0.8 mm thickness exhibited non-frangible behavior following ion exchange for 25.5 hours at 440°C in a bath containing 40 wt% NaNO 3 and about 60 wt% KNO 3 .
  • the sample had a CS of about 281 MPa, a DOL of about 146 ⁇ m, a DOC of about 109 ⁇ m, and a physical CT of about 45 MPa, the latter being substantially greater than the prior-art limit in terms of physical CT (43.5 MPa) for a thickness of 0.8 mm.
  • the elastic energy was about 30.2 J/m 2 in the compression region, and about 10.6 J/m 2 in the tension half-region, resulting in a total of about 77.1 J/m 2 .
  • the elastic energy density, i.e., the elastic energy per unit area and unit thickness was about 96.4 J/m 2 mm.
  • the difference CT-CS of this non-frangible glass was at least about 334 MPa.
  • Ion exchange was carried out at 440°C in a bath comprising about 45 wt% NaNO 3 and about 55 wt% KNO 3 .
  • Ion exchange times were 25.25, 30, 36, and 42 hours, and the resulting physical CT values were estimated to be 39.3 MPa, 42.5 MPa, at least 44.9 MPa, and 48.4 MPa, respectively.
  • the values may be somewhat underestimated, particularly for the 36 hour ion exchange, due to the DOL exceeding 160 ⁇ m, which presents challenges for precise resolution of the high-order modes.
  • the DOL ranged from about 143 ⁇ m to over 170 ⁇ m, while the DOC ranged from about 115 ⁇ m to about 136 ⁇ m.
  • the difference CT-CS ranged from about 313 MPa to about 325 MPa.
  • the total stored elastic energy ranged from about 73.4 81.7 J/m 2 to at least about 81.7 J/m 2 and the average energy density was 81.7 J/(m 2 ⁇ mm).
  • Samples in Table 4 having a thickness of 1.0 mm were ion exchanged for 42.6 hours at 440°C in a bath comprising about 40 wt% NaNO 3 and about 60 wt% KNO 3 .
  • the resulting strengthened glass was non-frangible, with CS of about 272 MPa, and a physical CT of at least about 52.8 MPa, which was substantially above the physical CT frangibility limit estimate of 37 MPa for 1 mm thick glass with DOL of about 50 ⁇ m.
  • the DOL was estimated to be about 185 ⁇ m or greater, the DOC was about 139 ⁇ m, and the elastic energy was about 36.6 J/m 2 in the compression region and greater than about 10.4 J/m 2 in the tension half-region.
  • the total elastic energy was at least 49.9 J/m 2 , and represents an average elastic energy density of at least 49.9 J/m 2 mm.
  • the examples show that when the DOL accounts for an appreciable fraction of the glass thickness, the CT value at which frangibility occurs can vary with DOL, depending on the stored total elastic energy.
  • the total elastic energy becomes even more significant in the case of double-ion-exchanged glass having a deep region of moderate compression and a shallow region of high compression in which the stress varies strongly with depth ( FIGS. 7 and 8 ).
  • the sample represented in FIGS. 7 and 8 was double-ion exchanged 0.55 mm thick glass.
  • the first ion exchange step involved a soak at 450°C for 7.75 hours in a 40 wt% NaNO 3 /60 wt% KNO 3 molten mixture.
  • the first ion exchange step produced the deep, slowly-changing portion A of the stress profile.
  • the glass was ion exchange at 390°C for 12 minutes in a bath containing approximately 99.5 wt% KNO 3 and 0.5 wt% NaNO 3 , producing the shallow steep region B of the stress profile. Samples with this stress profile are unlikely to be frangible, although any significant even minor additional ion exchange to increase the depth of the first or second region would result in a frangible glass.
  • the elastic energy was about 44.7J/m 2 in the compression region, and about 7.8 MJ/m 2 in the tension half-region.
  • the total elastic energy was about 105 J/m2, representing an average energy density of about 191 J/m 2 mm. This is the highest average elastic energy density that has been observed in non-frangible samples having a large chemical penetration depth of greater than about 0.12t, and CTA substantially above the CT 3 prior-art frangibility limit.
  • FIG. 8 is a plot of the stress profile for double-ion exchanged 0.55 mm-thick glass.
  • the first step involved ion exchange for 7.75 hours at 450°C in a molten mixture of 40 wt% NaNO 3 and 60 wt% KNO 3 .
  • the first step produced the deep slowly-changing portion (A) of the stress profile.
  • the glass was ion exchanged at 390°C for 12 minutes in a bath containing approximately 99.5 wt% KNO 3 and 0.5 wt% NaNO 3 , producing the shallow steep region (B) of the stress profile
  • Samples having the stress profile shown in FIG. 8 were found to be non-frangible, although any significant additional ion exchange to increase the depth of the first or second region would result in frangible glass.
  • the IWKB analysis of the glass revealed a CS of about 891 MPa, a DOC of about 70.6 ⁇ m, and a physical CT of about 61 MPa, the latter being substantially above the frangibility limit in terms of physical CT estimated based on previous guidelines for strengthened glasses having a thickness of 0.55 mm and a DOL of 40 ⁇ m.
  • the elastic energy of the sample shown in FIG. 6 was about 44.7 J/m 2 in the compression region, and about 9.5 MJ/m 2 in the region under tension.
  • the total elastic energy was about 54.1 J/m 2 , representing an average energy density of about 98.4 J/m 2 ⁇ mm. This is the highest average elastic energy density that has been observed in non-frangible samples. It is estimated that the maximum average elastic energy density for non-frangible glass over the thickness range from 0.4 mm to 1 mm lies between about 98 J/m 2 mm and 116.5 J/m 2 mm, the latter value being the lowest value where 0.4 mm-thick glass with large DOL was observed to be frangible.
  • the elastic energy density is less than about 200 J/m 2 ⁇ mm. In other embodiments, the elastic energy density is less than about 140 J/m 2 ⁇ mm and, in still other embodiments, the elastic energy is less than about 120 J/m 2 ⁇ mm.
  • FIG. 9 represents the TE and TM refractive index profiles for the sample whose stress profile is shown in FIG. 8 .
  • the refractive index increases as a result of the ion exchange, and the index profile is a monotonic function of depth, making it convenient to use IWKB analysis for the extraction and evaluation of stress profiles.
  • the index profiles of FIG. 9 show that, other than approximating the surface compressive stress the DOL, the FSM-6000 will significantly under-estimate the chemical penetration depth for the deep region and will not provide direct information about the steep shallow region in the case of double-ion-exchange (DIOX) profiles.
  • the compression depth DOC is still a physical quantity that can be measured by various polarimetry techniques and represent the depth of chemical strengthening. As can be seen in Tables 1 and 2 below, the DOC is greater than 0.1t, usually exceeds 0.12t, and most often exceeds 0.15t for all examples of non-frangible glass with physical CT exceeding the prior-art frangibility limit.
  • the criterion for non-frangibility that is based on the difference CT-CS regardless of DOL can be equivalently restated as the non-frangibility region for CT-CS ⁇ 330 MPa when using a salt composition and temperature that allows CT-CS ⁇ 350 MPa to be achieved when 10 ⁇ m ⁇ DOL short ⁇ 40 ⁇ m. This permits an infinite increase of DOC without risk of frangibility.
  • the frangibility criterion that stored elastic energy should be less than about 233 J/m 2 ⁇ mm and, in some embodiments, less than about 197 J/m 2 ⁇ mm, can be applied to a wide variety of glasses having DOC > 0.1t, including Li 2 O-rich glasses that may have Na + for Li + ion exchange, and also Na + and K + for Li + ion exchange.
  • the criterion 10 ⁇ m ⁇ DOL short ⁇ 40 ⁇ m may be replaced with a criterion 10 ⁇ m ⁇ DOL short ⁇ 40 ⁇ m, as DOL may not be defined in FSM-6000 terms.
  • FIG. 9 is a plot of the TE and TM refractive index profiles for of the double-ion-exchanged 0.55 mm thick glass sample shown in FIG. 8 .
  • the refractive index increases as a result of the ion exchange.
  • the index profile is a monotonic function of depth, making it convenient to use IWKB analysis for the extraction and evaluation of stress profiles.
  • the index profiles of FIG. 9 show that, in the case of double-ion-exchange (DIOX) profiles, the DOL estimated by the FSM-6000 will significantly underestimate the chemical penetration depth for the deep region of the compressive layer and will not provide direct information about the steep shallow region, other than approximate estimate of the surface compressive stress.
  • DIOX double-ion-exchange
  • the widely used DOL reported by FSM-6000 is calculated assuming that the index profile is well represented by a single linear segment having a single fixed slope and a single depth of penetration.
  • the widely used CT A calculated based on that DOL and the surface CS is often a factor of two to three times greater than the physical CT for the DIOX profile, and is therefore not convenient to use as a predictor of frangibility.
  • the analysis described in the present disclosure in terms of physical CT and stored elastic energy has a much broader realm of application than the CT A -based criteria of the prior art.
  • stress profiles having large compression depth DOC may be obtained using ion exchange such as , for example, during exchange of Na + for Li + in a glass that is rich in Li 2 O, that does not result in an increase of the. DOL based on measurement of the number of guided optical modes is not available in these cases.
  • the compression depth DOC is a physical quantity that represents the depth of chemical strengthening can be measured by various polarimetry and refractive near-field (RNF) techniques.
  • RMF refractive near-field
  • CT-CS non-frangibility region for CT-CS ⁇ 330 MPa, using a salt composition and temperature that may allow CT-CS values as high as 350 MPa when 10 ⁇ m ⁇ DOL short ⁇ 40 ⁇ m, thus allowing an infinite increase of DOC without risk of frangibility.
  • the frangibility criterion that stored elastic energy should be ⁇ 233 J/m2 ⁇ mm, and, in some embodiments, less than about 197 J/m 2 ⁇ mm can be applied to a wide variety of glasses having DOC > 0.1t, including Li 2 O rich glasses that may have Na + for Li + ion exchange, and also Na + and K + for Li + ion exchange.
  • the criterion 10 ⁇ m ⁇ DOL short ⁇ 40 ⁇ m may be replaced with a criterion 10 ⁇ m ⁇ DOC short ⁇ 40 ⁇ m, as DOL may not be defined in terms of FSM-6000 data.
  • a frangibility criterion in the form of a normalized total energy is provided.
  • the ion exchanged glass article having a central tension CT above the limit CT 3 for thicknesses less than or equal to 0.75 mm, or above the limit CT 1 for thicknesses greater than 0.75 mm has a total normalized elastic energy per unit thickness less than or equal to 37.5 x 10 3 MPa 2 ⁇ m.
  • a substrate having a CT A greater than 106.6 MPa should store a normalized elastic energy less than or equal to 15 x10 6 MPa 2 ⁇ m.
  • the total normalized energy is less than 7.5 x 10 6 MPa 2 ⁇ m for 0.4 mm thick substrates.
  • the normalized stored elastic energy per unit thickness is less than about 19 x 10 3 MPa 2 ⁇ m.
  • the glass articles described herein may comprise or consist of any glass that is chemically strengthened by ion exchange.
  • the glass is an alkali aluminosilicate glass.
  • the alkali aluminosilicate glass comprises or consists essentially of: at least one of alumina and boron oxide, and at least one of an alkali metal oxide and an alkali earth metal oxide, wherein -15 mol% ⁇ (R 2 O + R'O - Al 2 O 3 - ZrO 2 ) - B 2 O 3 ⁇ 4 mol%, where R is one of Li, Na, K, Rb, and Cs, and R' is at least one of Mg, Ca, Sr, and Ba.
  • the alkali aluminosilicate glass comprises or consists essentially of: from about 62 mol% to about 70 mol.% SiO 2 ; from 0 mol% to about 18 mol% Al 2 O 3 ; from 0 mol% to about 10 mol% B 2 O 3 ; from 0mol% to about 15 mol% Li 2 O; from 0 mol% to about 20 mol% Na 2 O; from 0 mol% to about 18 mol% K 2 O; from 0 mol% to about 17 mol% MgO; from 0 mol% to about18 mol% CaO; and from 0 mol% to about 5 mol% ZrO 2 .
  • the glass comprises alumina and boron oxide and at least one alkali metal oxide, wherein -15 mol% ⁇ (R 2 O + R'O - Al 2 O 3 - ZrO 2 ) - B 2 O 3 ⁇ 4 mol%, where R is at least one of Li, Na, K, Rb, and Cs, and R' is at least one of Mg, Ca, Sr, and Ba; wherein 10 ⁇ Al 2 O 3 + B 2 O 3 + ZrO 2 ⁇ 30 and 14 ⁇ R 2 O + R'O ⁇ 25; wherein the silicate glass comprises or consists essentially of: 62-70 mol.% SiO 2 ; 0-18 mol% Al 2 O 3 ; 0-10 mol% B 2 O 3 ; 0-15 mol% Li 2 O; 6-14 mol% Na 2 O; 0-18 mol% K 2 O; 0-17 mol% MgO; 0-18 mol% CaO; and 0-5 mol% ZrO
  • the alkali aluminosilicate glass comprises or consists essentially of: from about 60 mol% to about 70 mol% SiO 2 ; from about 6 mol% to about 14 mol% Al 2 O 3 ; from 0 mol% to about 15 mol% B 2 O 3 ; from 0 mol% to about 15 mol% Li 2 O; from 0 mol% to about 20 mol% Na 2 O; from 0 mol% to about 10 mol% K 2 O; from 0 mol% to about 8 mol% MgO; from 0 mol% to about 10 mol% CaO; from 0 mol% to about 5 mol% ZrO 2 ; from 0 mol% to about 1 mol% SnO 2 ; from 0 mol% to about 1 mol% CeO 2 ; less than about 50 ppm As 2 O 3 ; and less than about 50 ppm Sb 2 O 3 ; wherein 12 mol% ⁇ Li 2 O + Na 2 O + K 2
  • the alkali aluminosilicate glass comprises or consists essentially of: 60-70 mol% SiO 2 ; 6-14 mol% Al 2 O 3 ; 0-3 mol% B 2 O 3 ; 0-1 mol% Li 2 O; 8-18 mol% Na 2 O; 0-5 mol% K 2 O; 0-2.5 mol% CaO; above 0 to 3 mol % ZrO 2 ; 0-1 mol% SnO 2 ; and 0-1 mol% CeO 2 , wherein 12 mol% ⁇ Li 2 O + Na 2 O + K 2 O ⁇ 20 mol%, and wherein the silicate glass comprises less than 50 ppm As 2 O 3 .
  • the alkali aluminosilicate glass comprises or consists essentially of: 60-72 mol% SiO 2 ; 6-14 mol% Al 2 O 3 ; 0-3 mol% B 2 O 3 ; 0-1 mol% Li 2 O; 0-20 mol% Na 2 O; 0-10 mol% K 2 O; 0-2.5 mol% CaO; 0-5 mol% ZrO 2 ; 0-1 mol% SnO 2 ; and 0-1 mol% CeO 2 , wherein 12 mol% ⁇ Li 2 O + Na 2 O + K 2 O ⁇ 20 mol%, and wherein the silicate glass comprises less than 50 ppm As 2 O 3 and less than 50 ppm Sb 2 O 3 .
  • the alkali aluminosilicate glass comprises SiO 2 and Na 2 O, wherein the glass has a temperature T 35kp at which the glass has a viscosity of 35 kilo poise (kpoise), wherein the temperature T breakdown at which zircon breaks down to form ZrO 2 and SiO 2 is greater than T 35kp .
  • the alkali aluminosilicate glass comprises or consists essentially of: from about 61 mol % to about 75 mol% SiO 2 ; from about 7 mol % to about 15 mol% Al 2 O 3 ; from 0 mol% to about 12 mol% B 2 O 3 ; from about 9 mol % to about 21 mol%Na 2 O; from 0 mol % to about 4 mol% K 2 O; from 0 mol% to about 7 mol% MgO; and 0 mol% to about 3 mol% CaO.
  • the glass is described in U.S. Patent Application No. 12/856,840 by Matthew J. Dejneka et al.
  • the alkali aluminosilicate glass comprises at least 50 mol% SiO 2 and at least one modifier selected from the group consisting of alkali metal oxides and alkaline earth metal oxides, wherein [(Al 2 O 3 (mol%) + B 2 O 3 (mol%))/( ⁇ alkali metal modifiers (mol%))] > 1.
  • the alkali aluminosilicate glass comprises or consists essentially of: from 50 mol% to about 72 mol% SiO 2 ; from about 9 mol% to about 17 mol% Al 2 O 3 ; from about 2 mol% to about 12 mol% B 2 O 3 ; from about 8 mol% to about 16 mol% Na 2 O; and from 0 mol% to about 4 mol% K 2 O.
  • the glass comprises or consists essentially of: at least 58 mol% SiO 2 ; at least 8 mol% Na 2 O; from 5.5 to 12 mol% B 2 O 3 ; and Al 2 O 3 , wherein [(Al 2 O 3 (mol%) + B 2 O 3 (mol%))/( ⁇ alkali metal modifiers (mol%))] > 1, Al 2 O 3 (mol%) > B 2 O 3 (mol%), 0.9 ⁇ R 2 O/Al 2 O 3 ⁇ 1.3.
  • the glass is described in U.S. Patent No. 8,586,492 , entitled "Crack And Scratch Resistant Glass and Enclosures Made Therefrom," filed August 18, 2010, by Kristen L. Barefoot et al., U.S.
  • Patent Application No. 14/082,847 entitled “Crack And Scratch Resistant Glass and Enclosures Made Therefrom,” filed November 18, 2013, by Kristen L. Barefoot et al., both claiming priority to U.S. Provisional Patent Application No. 61/235,767, filed on August 21, 2009 .
  • the contents of all of the above are incorporated herein by reference in their entirety.
  • the alkali aluminosilicate glass comprises or consists essentially of: from about 40 mol% to about 70 mol% SiO 2 ; from 0 mol% to about 28 mol% B 2 O 3 ; from 0 mol% to about 28 mol% Al 2 O 3 ; from about 1 mol% to about 14 mol% P 2 O 5 ; and from about 12 mol% to about 16 mol% R 2 O; and, in certain embodiments, from about 40 to about 64 mol% SiO 2 ; from 0 mol% to about 8 mol% B 2 O 3 ; from about 16 mol% to about 28 mol% Al 2 O 3 ; from about 2 mol% to about 12% P 2 O 5 ; and from about 12 mol% to about 16 mol% R 2 O.
  • the alkali aluminosilicate glass comprises at least about 50 mol% SiO 2 and at least about 11 mol% Na 2 O, and the compressive stress is at least about 900 MPa.
  • the glass further comprises Al 2 O 3 and at least one of B 2 O 3 , K 2 O, MgO and ZnO, wherein -340 + 27.1 ⁇ Al 2 O 3 - 28.7 ⁇ B 2 O 3 + 15.6 ⁇ Na 2 O - 61.4 ⁇ K 2 O + 8.1 ⁇ (MgO + ZnO) ⁇ 0 mol%.
  • the glass comprises or consists essentially of: from about 7 mol% to about 26 mol% Al 2 O 3 ; from 0 mol% to about 9 mol% B 2 O 3 ; from about 11 mol% to about 25 mol% Na 2 O; from 0 mol% to about 2.5 mol% K 2 O; from 0 mol% to about 8.5 mol% MgO; and from 0 mol% to about 1.5 mol% CaO.
  • the glass is described in U.S. Patent Application No. 13/533,298, by Matthew J. Dejneka et al. , entitled “Ion Exchangeable Glass with High Compressive Stress," filed June 26, 2012, and claiming priority to U.S. Provisional Patent Application No. 61/503,734, filed July 1, 2011 . The contents of all of the above are incorporated herein by reference in their entirety.
  • the alkali aluminosilicate glass is ion exchangeable and comprises: at least about 50 mol% SiO 2 ; at least about 10 mol% R 2 O, wherein R 2 O comprises Na 2 O; Al 2 O 3 ; and B 2 O 3 , wherein B 2 O 3 - (R 2 O - Al 2 O 3 ) ⁇ 3 mol%.
  • the glass comprises: at least about 50 mol% SiO 2 ; at least about 10 mol% R 2 O, wherein R 2 O comprises Na 2 O; Al 2 O 3 , wherein Al 2 O 3 (mol%) ⁇ R 2 O(mol%); and 3-4.5 mol% B 2 O 3 , wherein B 2 O 3 (mol%) - (R 2 O(mol%) - Al 2 O 3 (mol%)) ⁇ 3 mol%.
  • the glass comprises or consists essentially of: at least about 50 mol% SiO 2 ; from about 9 mol% to about 22 mol% Al 2 O 3 ; from about 3 mol% to about 10 mol% B 2 O 3 ; from about 9 mol% to about 20 mol% Na 2 O; from 0 mol% to about 5 mol% K 2 O; at least about 0.1 mol% MgO, ZnO, or combinations thereof, wherein 0 ⁇ MgO ⁇ 6 and 0 ⁇ ZnO ⁇ 6 mol%; and, optionally, at least one of CaO, BaO, and SrO, wherein 0 mol% ⁇ CaO + SrO + BaO ⁇ 2 mol%.
  • the glass when ion exchanged, has a Vickers crack initiation threshold of at least about 10 kgf.
  • Such glasses are described in U.S. Patent Application No. 14/197,658, filed May 28, 2013, by Matthew J. Dejneka et al. , entitled “Zircon Compatible, Ion Exchangeable Glass with High Damage Resistance,” which is a continuation of U.S. Patent Application No. 13/903,433, filed May 28, 2013, by Matthew J. Dejneka et al. , entitled “Zircon Compatible, Ion Exchangeable Glass with High Damage Resistance,” both claiming priority to Provisional Patent Application No. 61/653,489, filed May 31, 2012 . The contents of these applications are incorporated herein by reference in their entirety.
  • the glass comprises: at least about 50 mol% SiO 2 ; at least about 10 mol% R 2 O, wherein R 2 O comprises Na 2 O; Al 2 O 3 , wherein -0.5 mol% ⁇ Al 2 O 3 (mol%) - R 2 O(mol%) ⁇ 2 mol%; and B 2 O 3 , and wherein B 2 O 3 (mol%) - (R 2 O(mol%) - Al 2 O 3 (mol%)) ⁇ 4.5 mol%.
  • the glass has a zircon breakdown temperature that is equal to the temperature at which the glass has a viscosity of greater than about 40 kPoise and comprises: at least about 50 mol% SiO 2 ; at least about 10 mol% R 2 O, wherein R 2 O comprises Na 2 O; Al 2 O 3 ; and B 2 O 3 , wherein B 2 O 3 (mol%) - (R 2 O(mol%) - Al 2 O 3 (mol%)) ⁇ 4.5 mol%.
  • the glass is ion exchanged, has a Vickers crack initiation threshold of at least about 30 kgf, and comprises: at least about 50 mol% SiO 2 ; at least about 10 mol% R 2 O, wherein R 2 O comprises Na 2 O; Al 2 O 3 , wherein -0.5 mol% ⁇ Al 2 O 3 (mol%) - R 2 O(mol%) ⁇ 2 mol%; and B 2 O 3 , wherein B 2 O 3 (mol%) - (R 2 O(mol%) - Al 2 O 3 (mol%)) ⁇ 4.5 mol%.
  • Such glasses are described in U.S. Patent Application No. 903,398, by Matthew J. Dejneka et al. , entitled “Ion Exchangeable Glass with High Damage Resistance,” filed May 28, 2013, claiming priority from U.S. Provisional Patent Application No. 61/653,485, filed May 31, 2012 . The contents of these applications are incorporated by reference herein in their entirety.
  • the monovalent and divalent cation oxides are selected from the group consisting of Li 2 O, Na 2 O, K 2 O, Rb 2 O, Cs 2 O, MgO, CaO, SrO, BaO, and ZnO.
  • the glass comprises 0 mol% B 2 O 3 .
  • M 2 O 3 Al 2 O 3 + B 2 O 3
  • R x O is the sum of monovalent and divalent cation oxides present in the alkali aluminosilicate glass
  • R 2 O is the sum of divalent cation oxides present in the alkali aluminosilicate glass.
  • the alkali aluminosilicate glass comprises: from about 50 mol% to about 72 mol% SiO 2 ; from about 12 mol% to about 22 mol% Al 2 O 3 ; up to about 15 mol% B 2 O 3 ; up to about 1 mol% P 2 O 5 ; from about 11 mol% to about 21 mol% Na 2 O; up to about 5 mol% K 2 O; up to about 4 mol% MgO; up to about 5 mol% ZnO; and up to about 2 mol% CaO.
  • the glass comprises: from about 55 mol% to about 62 mol% SiO 2 ; from about 16 mol% to about 20 mol% Al 2 O 3 ; from about 4 mol% to about 10 mol% B 2 O 3 ; from about 14 mol% to about 18 mol% Na 2 O; from about 0.2 mol% to about 4 mol% K 2 O; up to about 0.5 mol% MgO; up to about 0.5 mol% ZnO; and up to about 0.5 mol% CaO, wherein the glass is substantially free of P 2 O 5 .
  • the glass is described in U.S.
  • the glasses described herein are substantially free of at least one of arsenic, antimony, barium, strontium, bismuth, lithium, and their compounds.
  • the glasses may include up to about 5 mol% Li 2 O and, in some embodiments, up to about 10 mol% Li 2 O.
  • the glasses described herein when ion exchanged, are resistant to introduction of flaws by sharp or sudden impact. Accordingly, these ion exchanged glasses exhibit Vickers crack initiation threshold of at least about 10 kilogram force (kgf). In certain embodiments, these glasses exhibit a Vickers crack initiation threshold of at least 20 kgf and, in some embodiments, at least about 30 kgf.
  • the glasses described herein may, in some embodiments, be down-drawable by processes known in the art, such as slot-drawing, fusion drawing, redrawing, and the like, and have a liquidus viscosity of at least 130 kilopoise.
  • processes known in the art such as slot-drawing, fusion drawing, redrawing, and the like
  • liquidus viscosity of at least 130 kilopoise.
  • various other ion exchangeable alkali aluminosilicate glass compositions may be used.

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US20240158285A1 (en) 2024-05-16
TWI773291B (zh) 2022-08-01
KR102456129B1 (ko) 2022-10-18
EP3157881B1 (fr) 2023-04-26
US11878941B2 (en) 2024-01-23
JP7461910B2 (ja) 2024-04-04
US20150368148A1 (en) 2015-12-24
CN111253069B (zh) 2022-07-29
KR20220143965A (ko) 2022-10-25
TW202311197A (zh) 2023-03-16
TW201605614A (zh) 2016-02-16
JP2021120349A (ja) 2021-08-19
TW202103938A (zh) 2021-02-01
KR20170018959A (ko) 2017-02-20
KR102645342B1 (ko) 2024-03-08
TWI729925B (zh) 2021-06-01
EP3157881A1 (fr) 2017-04-26
JP2017523110A (ja) 2017-08-17
TWI705889B (zh) 2020-10-01
TWI697403B (zh) 2020-07-01
TW202015909A (zh) 2020-05-01
CN106604901A (zh) 2017-04-26
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JP6938157B2 (ja) 2021-09-22
CN111253069A (zh) 2020-06-09

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